Evolution of Interfacial Microstructure of Ni-Co Base Superalloy During Plastic Deformation Bonding and Its Bonding Mechanism
REN Shaofei1,2, ZHANG Jianyang2, ZHANG Xinfang1(), SUN Mingyue2,3(), XU Bin2,3, CUI Chuanyong4
1.School of Metallurgical and Ecological Engineering, University of Science and Technology Beijing, Beijing 100083, China 2.Shenyang National Laboratory for Materials Science, Institute of Metal Research, Chinese Academy of Sciences, Shenyang 110016, China 3.Key Laboratory of Nuclear Materials and Safety, Institute of Metal Research, Chinese Academy of Sciences, Shenyang 110016, China 4.Shi -changxu Innovation Center for Advanced Materials, Institute of Metal Research, Chinese Academy of Sciences, Shenyang 110016, China
Cite this article:
REN Shaofei, ZHANG Jianyang, ZHANG Xinfang, SUN Mingyue, XU Bin, CUI Chuanyong. Evolution of Interfacial Microstructure of Ni-Co Base Superalloy During Plastic Deformation Bonding and Its Bonding Mechanism. Acta Metall Sin, 2022, 58(2): 129-140.
Superalloys with excellent high-temperature resistance and oxidation resistance have been widely used in aviation and energy fields. The new Ni-Co base superalloy is considered a candidate for the next generation of turbine discs due to its higher performance of mechanical properties and microstructure stability at high temperatures. However, tungsten inert gas (TIG) welding, metal inert gas (MIG) welding, and other welding techniques are not suitable for welding the new Ni-Co base superalloy because the Al + Ti content of the alloy reaches 7.5%, while traditional welding techniques (electron beam welding, friction welding, and diffusion welding) also have some disadvantages. For example, friction welding has certain requirements on the shape of the sample, and it is not suitable for welding large-volume alloys. Diffusion welding requires a long heat retention period and a harmful precipitation phase exists at the interface. A new welding method is applied in this study to solve the problem of welding nickel-based superalloy, achieving a better bonding effect. The Gleeble 3500 thermal simulator was used to study the plastic deformation bonding of Ni-Co base superalloys in a temperature range of 1000-1200oC and a strain range of 5%-40% with a strain rate of 0.001 s-1. The recrystallization behavior of the interface was studied by OM, EBSD, and TEM, and the bonding mechanism of the interface was clarified. The results showed that the resistance to deformation of the alloy was low when the plastic deformation bonding was performed at 1150oC, and there was no risk of cracking of the alloy. Plastic deformation bonding experiments with different deformations had shown that the alloy can achieve complete bonding of the interface under the condition of 40% deformation, and its mechanical properties can reach the same level as the matrix. The tensile fracture analysis showed that the fracture profile of the 40% deformed joint was consistent with the base material, showing a ductile fracture pattern. The results of EBSD and TEM showed that the coarse grains near the interface were first refined during the plastic deformation. With the increase of deformation, the refined grain removed the original interface by the migration of the interfacial grain boundaries with the assistance of a continuous dynamics recrystallization process and ultimately led to the bonding of the interface.
Fund: National Key Research and Development Program of China(2018YFA0702900);National Natural Science Foundation of China(51774265);National Science and Technology Major Project of China(2019ZX06004010);Program of CAS Interdisciplinary Innovation Team and Youth Innovation Promotion Association, CAS
About author: ZHANG Xinfang, professor, Tel: (010)82375027, E-mail: xfzhang@ustb.edu.cnSUN Mingyue, professor, Tel: (024)83970108, E-mail: mysun@imr.ac.cn
Fig.2 OM images of microstructures of as-cast (a) and homogenized (b) Ni-Co base superalloy
Fig.3 OM images of microstructures at deformation temperatures of 1000oC (a), 1050oC (b), 1100oC (c), 1150oC (d), and 1200oC (e), and the true stress-strain curves (f) of the Ni-Co base superalloy at the strain rate of 0.001 s-1
Fig.4 OM images of microstructures at true strains of 5% (a), 10% (b), 20% (c), 30% (d), and 40% (e), and statistics of mean grain size (f) of the Ni-Co base superalloy at the deformation temperature of 1150℃
Fig.5 Tensile curves of the joints at room temperature under different deformations
Fig.6 Tensile fracture morphologies of base material (a, c) and joints (b, d) at different deformations of 20% (a, b) and 40% (c, d)
Fig.7 Inverse pole figure (IPF) maps (a, c, e, g, i) and local average misorientation (LAM) maps (b, d, f, h, j) of the interface microstructure under different deformations at 1150℃
Fig.8 Misorientation distributions of the interface microstructures under different deformations at 1150℃
Fig.9 TEM images of bulging of interfacial grain boundaries (a) and interfacial substructure (b) at a deformation temperature of 1150℃ and 20% deformation
Fig. 10 Interface bonding mechanism during plastic deformation bonding
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